Process for making ethylene interpolymers and interpolymers made thereby; compositions and electrical devices containing such interpolymers

ABSTRACT

The invention relates to a continuous polymerization process for preparing a random ethylene interpolymer with propylene and/or 1-butene which comprises: (A) polymerizing ethylene, and as an α-olefin comonomer propylene and/or 1-butene under continuous random polymerization conditions in the presence of single site catalyst system employing an ionic activator having cyclic ligands shielding a central charge bearing atom, at a temperature of 140° C. to 250° C. at a conversion of ethylene of 80 to 99% and a comonomer conversion of from at least 30% and 
         (B) devolatilizing the polymer to provide an ethylene copolymer having a density of from 0.85 to 0.92 g/cm 3 , an MI of from 0.01 to 100 g/10 min, preferably from 0.1 to 20, and an I 21 /I 2  of from 30 to 400. 
 
The invention also relates to polymers made by such processes containing as α-olefin comonomer propylene and/or 1-butene, having a density of from 0.85 to 0.92 g/cm 3 , an MI of from 0.01 to 100 g/10 min and an I 21 /I 2  of from 30 to 400 obtained by solution polymerization using a transition metal complex as a catalyst and a non-coordinating anion to provide a level of NCA derived residue, as determined by boron content, less than 0.5 ppm. as determined by ICP, preferably undetectable by ICP. The polymers may be blended with EP rubber elastomers and be used for electrical cable insulation.

FIELDS OF INDUSTRIAL APPLICATION

The invention relates processes for making ethylene interpolymers andthe polymers that can be made by such processes as well as electricaldevices containing such interpolymers. The invention relates especially,but not exclusively, to processes for making ethylene interpolymers atrelatively high polymerization temperatures of over 100° C. in order toform polymers with high levels of long chain branches (LCB); andespecially such polymers having a relatively low density and a moderatemolecular weight that are processable as a thermoplastic material. Thehigh LCB can be expressed in terms of a Melt Index Ratio (MIR) of meltviscosities measured under different loads. The invention also relatesto electrical devices having an insulating layer of the interpolymer orcompositions containing such interpolymer such as electrical cables.

BACKGROUND FOR INTERPOLYMER POLYMERIZATION

Lower density ethylene interpolymers with moderate molecular weightswill be referred herein as plastomers. Plastomers have been made withcatalyst systems based on Ziegler-Natta vanadium catalysts usingaluminum alkyl based activators. Such polymers have high levels ofregio-inversion for the insertion of the propylene comonomer. The lowactivity of the catalyst leads to the need to de-ash the polymer toremove vanadium residues, especially for if the polymer is to be usedfor electrical applications. Propylene and 1-butene have been used ascomonomers to provide short chain branching (SCB) in Ziegler-Nattaproduced plastomers. More recently metallocene based single sitecatalysts have been identified to make plastomers in a continuoussolution process at higher temperatures and at higher activities whereactivity is defined as the amount of polymer produced per amount oftransition metal single site catalyst component.

It has been recognized that metallocene based catalyst systems produceterminal unsaturation by, for example, beta-hydride elimination. It hasbeen recognized that for many metallocene based processes theunsaturated chain end may incorporate in a growing chain and form longchain branches (LCB). EP495099 (Mitsui) and EP608369 (Dow) describeprocesses proving indications of LCB formation through increased shearsensitivity of the polymer, a recognized effect provided by LCB.

EP495099 uses a hafnocene in conjunction with alumoxane as an activator.In the examples 1-octene, 1-butene and propylene were used as acomonomer for batch polymerization at temperatures less than 100° C.providing polymers with high MIR values. Extensive depletion ofcomonomer in batch type reactions may favor LCB formation. Thepolymerization conditions however lead to significant levels of catalystresidues. The polymer produced at the end of the batch polymerizationprocess may have a significantly different comonomer content than thatproduced early in the process and the polymer may have a broadercompositional distribution.

In WO9941294/19Aug1999 and WO9945041/10Sep99 (issued as U.S. Pat. No.6,291,609) processes using metallocene based single site catalysts aredescribed in which the polymerization temperature is increased to above100° C. by using hafnium as a transition metal and/or improvednon-coordinating anionic activators (NCA). WO99/1294 does not combinethe use of the improved catalyst system with propylene with asufficiently low amount of diene. Polymerization is performed at 115° C.with a relatively low amount of propylene. There is no quantification ofthe LCB level. WO9945041 teaches the use of a bridged hafnoceneactivated by a tetra-aryl substituted anion, wherein each anion has atleast two cyclic aromatic rings. In the examples octene-1 is used as acomonomer. Polymerization was at 170° C. for MI levels of from 0.49 to3.6 g/10 min. WO9945041 does not teach the use of propylene as acomonomer at especially high temperature polymerization temperatures.

WO0234795 describes a plant, in which these processes can be practicedindustrially and in which an advantageous arrangement is described forrecycling unreacted monomers back to the polymerization reactor(s) aftersuitable purification through liquid phase separation, distillationand/or sieves. The above references are incorporated by reference for USpurposes.

WO0037514 describes a gel-free, branched semi-crystalline ethylenepropylene copolymer containing high levels of propylene. Thepolymerization temperature was less than 100° C. In the examples abridged zirconocene is used with an NCA in a continuous polymerizationreactor.

BACKGROUND FOR ELECTRICALLY INSULATING DEVICES

Ethylene propylene co-polymers and EP(D)M terpolymers havingpolyethylene type crystallinity are commercially used in medium voltageelectrical insulation compounds. These compounds are applied as aninsulation member over either a metallic conductor or a semi-conductivesubstrate in a multi-step extrusion process. The cable containing theinsulation is typically vulcanized in a continuous vulcanization (CV)tube by the application of steam and hot water. Cross-linking packagesmay use silanes or peroxides as the active cross-linking ingredient.

ExxonMobil Chemical recently commercialized a vanadium catalyzed EP(D)Mpolymer grade, Vistalon 1703P, for electrical applications using vinylnorbornene (VNB) as a termonomer, see EP843878. In other disclosures theEP-VNB is mixed with ethylene copolymers to aid cable manufacture, seeU.S. Pat. No. 5,763,533 and WO9856012. The presence of VNB providesextensive long chain branching as evidenced by a Branching Index of lessthan 1 and the polymers have good processability. The vanadium catalysthas a low activity. The VNB derived units in the polymer provide goodcross-linkability with peroxides, which enhances thermal stability. Thepolymers are de-ashed to remove at least partially, catalyst residuesand anti-agglomeration additives to obtain reasonable electricalinsulating properties. All of the above references are incorporated byreference for US purposes.

Metallocene catalyst based ethylene alpha-olefin copolymers also findlimited application in electrical insulation compounds. Someethylene-butene plastomer products made in a high-pressure process havebeen evaluated in insulation and semi-conductive formulations, see U.S.Pat. No. 6,270,856 (ExxonMobil, Hendewerk et al.) These polymers possessinherently good electrical insulating properties, but have a narrowmolecular weight distribution (MWD) resulting in processabilitydisadvantages. Other plastomers made in solution processes have some LCBfor reasons explained above. However, these polymers may still bedifficult to process and may have reduced electrical insulatingproperties WO03000740 (ExxonMobil, Pehlert) suggests the use of modifiedNCA's to improve dielectric loss properties. In one exampleethylene-octene plastomers are produced at 140° C. WO9406858 disclosesethylene octene copolymers with moderate LCB. WO9732922 usesrheology-modification to increase branching levels. The resultingpolymers have <0.5% gel, a composition distribution breadth index >50%,and an molecular weight distribution Mw/Mn<4.0. The above references areincorporated by reference for US purposes.

Alpha-olefin ethylene copolymers have been used in blends, especiallywith ethylene propylene vinyl norbornene terpolymers, see Rubber World,Volume 226, No. 2, pages 39 to 50.

It is among the aims of the invention to provide improved interpolymerswhich possess a high level of long chain branching at desirable levelsof MI and with low impurity levels; and catalyst and process conditionsto provide such interpolymers under continuous polymerizationconditions, preferably without post-treatments, with an improved balanceof properties, in particular the balance between processability andimpurity levels, especially but not exclusively for use in electricalinsulating applications.

SUMMARY

In a first aspect of the invention there is provided a continuouspolymerization process for preparing a random ethylene interpolymerwhich comprises the steps of:

-   -   (A) polymerizing ethylene, and an α-olefin comonomer selected        from the group consisting of propylene and 1-butene and mixtures        thereof under continuous random polymerization conditions in the        presence of single site catalyst system employing an ionic        activator having cyclic ligands shielding a central charge        bearing atom, at a temperature of 140° C. to 250° C. at a        conversion of ethylene of 80 to 99% and a comonomer conversion        of from 20 to 80%; and    -   (B) devolatilizing the polymer to provide an ethylene copolymer        having a density of from 0.85 to 0.92 g/cm³, an MI of from 0.1        to 20 g/10 min and an MIR(I²¹/I²) of from 30 to 200.

Generally speaking, I²¹/I² values are a function of MI and at low MIvalue high values of MIR(I²¹/I²) are possible. The comonomer conversionmay be less than 60% and the MIR(I²¹/I²) may be less than 180.

Under continuous polymerization conditions, the impact of catalystpoisons can be mitigated. The use of the lower α-olefin comonomers likepropylene and butene are generally supplied from purer streams withlower catalyst poisons and permits higher polymerization activities.Higher activities result in lower catalyst residues in the final polymerproduct. Internal olefin by-products, made during higher alpha-olefinproduction, may negatively impact catalyst activity and lead to highercatalyst residues.

In the process increased conversion helps attain the desired increasedI²¹/I² attributable to the presence of long chain branches.

Advantageously the interpolymer contains at least 55 mol % of ethylenederived units, preferably at least 60 mol % and especially at least 65mol %; from 0 to less than 10 mol % of an α-olefin comonomer other thanpropylene and/or 1-butene, preferably less than 5 mol %, and/or from 0to less than 0.5 mol % and preferably less than 0.1 mol % of a diene.The predominance of ethylene and the use of lower α-olefin comonomerassist in efficient production of the desired highly processable polymerwith reduced catalyst residue content.

The polymerization may be performed adiabatically using a catalystsystem including a hafnocene having two cyclopentadienyl groupsconnected by a bridging structure, preferably a single atom bridge. Theionic activator preferably has at least two polycyclic ligands,especially at least partly fluorinated. The use of a highly activemetallocene catalyst and substantially equimolar ionic activator maypermit reduced catalyst residue, which in turn may improve theelectrical insulating properties.

It is advantageous to maximize the reactor temperature and substantiallyeliminate the use of transfer agent such as hydrogen. The hightemperature may improve the amount of LCB through better incorporationof vinyl terminated polymer chains formed earlier in the polymerizationprocess. Chain transfer agents such as hydrogen can influence thetermination mechanism to reduce the amount of vinyl unsaturation anddiscourage LCB formation. In such circumstances the heat of thepolymerization reaction may raise the temperature by at least 100° C.between the feed for the continuous polymerization and the effluent tobe devolatilized.

The polymerization may be preformed in a single reactor such as acontinuous stirred tank reactor or the polymerization may be performedin a series reactor to provide a multimodal molecular weightdistribution, or a broad composition distribution.

In a further aspect of the invention, there is provided an ethyleneinterpolymer containing as α-olefin comonomer propylene and/or 1-butene,having a density of from 0.85 to 0.92 g/cm3, an MI of from 0.01 to 100g/10 min and an MIR(I²¹/I²) of from 30 to 400 obtained by solutionpolymerization using transition metal complex as a catalyst and anon-coordinating anion to provide a level of NCA derived residue asdetermined by boron content less than 0.5 ppm as determined by ICP,preferably undetectable by ICP.

The polymer may display the same preferred polymer features as indicatedwhen discussing the previous aspect. Preferably at an MI of from 0.01 to0.55, MIR(I²¹/I²)>−90.9×MI+90. The MIR(I²¹/I²) is then suitably at least45. Preferably at an MI of from 0.55 to 8, MIR(I21/I2)>−1.3×MI+40.7.Preferably at an MI of greater than 8, the MIR(I²¹/I²)>30.

The interpolymer may have specific MI ranges combined with specific highload/low load MI ratio ranges. Where the MI is from 0.01 to 0.30,I21/I2>−103.45×MI+91.0 and/or I21/I2<−103.45×MI+241.0. Where the MI isfrom 0.30 to 1.40, I21/I2>−18.18×MI+65.4 and/or I21/I2<−18.18×MI+215.4.Where the MI is from 1.40 to 8.0, I21/I2>−1.515×MI+42.1 and/orI21/I2<−1.515×MI+192.1. Where the MI is from 8.0 to 1000, I21/I2>30.0and/or I21/I2<180.0.

The preferred process conditions, including catalyst selection, may beobtained using as the single site catalyst is a transition metal complexof a Group IV metal, preferably Zr or Hf, most preferably Hf. A level ofsingle site residue as measured by the content of transition metal maybe reached which is less than 2 ppm (parts per million), preferably lessthan 1 ppm as determined by ICP.

The density is suitably at least 0.85 and/or less than 0.9 andpreferably at least 0.86 and/or less than 0.89. It is advantageous inelectrical applications that the polymer contains from 0 to 0.1 wt % ofan anti-agglomeration additive, such as a stearate salt.

In yet a further aspect the invention provides an electrical devicecomprising an electrical conductor and a polymeric insulating layercomprising a polymer with any one or more of the features indicatedpreviously or resulting from the process indicated previously.Compositions may be used for the insulting layer including the polymerof the invention in combination with other polymers, fillers etc. as maybe desired for the particular electrical application underconsideration. Suitably the insulating layer is of a composition alsocomprising an ethylene propylene elastomer with a Mooney [(1+4) 125° C.]range of from 10 to 100 and optionally a diene. It is preferred that theelastomer is an ethylene-propylene-vinylnorbornene terpolymer, mostpreferably with a content of ethylene derived units of from 68-75 wt. %,a molecular weight distribution Mw/Mn of at least 5 and contains from0.1 to 2.5 wt % of units derived from vinyl norbornene (VNB). Insulatinglayers may be obtained having a tensile strength of from 5 to 10 MPamin.; a break elongation of from 150 to 450% and a dielectric constantof less than 4.

Low levels of catalyst residue may remain in the polymer. Thepolymerization conditions can be selected to provide a high conversionof the monomers in solution, so favoring the incorporation of vinylterminated macromers, which thus go on to form LCB's. High conversionsreduce the cost for recycling unconsumed monomer.

Because of higher alpha-olefins are not employed, accumulation ofunsaturated or branched isomers of higher alpha-olefins can be avoided.The level of comonomer may be varied to target the desired density,melting point and heat of fusion. Preferably the density is at least0.86, and/or preferably less than 0.9; above that which is usuallyapplicable to EP copolymers made using vanadium catalysts.

The LCB content may be indirectly measured by the melt index ratio, MIRmeasured at MIR(I²¹/I²). Highly branched products have high MIR(I²¹/I²)and linear products have low MIR(I²¹/I²). Whereas substantially linearproducts may have moderate MIR(I²¹/I²) values around 12 to 17 asdescribed in EP608369, and whereas typical commercial plastomersproduced in solution may have MIR(I²¹/I²) values that are somewhat abovethat, the plastomer products of this invention have MIR(I²¹/I²) valuesaround 40 to 60 and even as high as 80. The high LCB content of thesematerials improves processability in extrusion and especially in thedemanding application of extruding wire and cable insulation. As aresult post treatment of the polymer to induce branching, the use ofbranch forming diene comonomers and/or presence of processing aids maybe reduced or even avoided. The high level of LCB leads to improvedprocessing while the polymer at the same time has a higher fillerholding capability, lower catalyst residues and lower dielectric powerloss.

In general the process envelope for continuous solution polymerizationreactor is limited by a number of mostly interrelated process aspects.If the catalyst activity is too low, the polymer will contain potentialtriggers for dielectric breakdown. Activity is conventionally expressedin terms of the amount of polymer produced per the amount of transitionmetal component consumed. Associated activators may be used at differentmolar ratios relative to the transition metal component. Thus for a fullactivity picture, the activity in terms of activator consumption perunit polymer produced may also be considered.

The level of long chain branching depends on the selection of thetransition metal component and some process conditions such astemperature and the extent to which the monomer present is converted.

The choice of transition metal component and NCA may influence the chaingrowth and molecular weight. If the catalyst system and processconditions are selected to optimize molecular weight, higher operatingtemperature may be used to achieve a given MI. The higher operatingtemperature may increase the activity and/or permit higher polymerconcentrations in the reactor and so higher productivity in terms ofweight of polymer produced per unit time in a given size plant. Thehigher process temperature aids the incorporation of vinyl terminatedmacromers.

The level of branching is also influenced by the extent to which monomeris converted into polymer. At high conversions, where little monomerremains in the solvent, conditions are such that vinyl terminated chainsare incorporated into the growing chains more frequently, resulting inhigher levels of LCB. Catalyst levels may be adjusted to influence thelevel of conversion as desired.

The selection of a lower α-olefin comonomer influences polymerizationkinetics and catalyst activity. Bridged bis-ligand metallocenestructures can provide a catalytic site, which encourages incorporationof the larger comonomers. Smaller comonomers such as propylene and1-butene can be incorporated more easily as well. As disclosed inWO9951648 it is believed that monomer feeds can accumulate non-polarimpurities with a negative impact on activity.

By using catalyst systems that combine a propensity for providing a highmolecular weight with high comonomer incorporation and avoiding orreducing the amount of higher α-olefins used as comonomer, it ispossible to extend the operating envelope for polymerization to regionsof high temperature and/or high monomer conversion to favor LCBformation so as to give MIR(I²¹/I²) in excess of 30 with catalystactivities based on grams of polymer produced per gram of transitionmetal compound consumed for continuous processes in excess of 200 000,possibly 400 000, or even above 600 000 for the target range of MI'ssuitable for thermoplastic processing such as extrusion in cablemanufacture.

As to the NCA, it is most preferred to use a NCA whose charge bearingatom or atoms, especially boron or aluminum, are shielded byhalogenated, especially perfluorinated, cyclic radicals, and especiallypolycyclic radical such as biphenyl and/or naphthyl radicals. Mostpreferably the NCA is a borate precursor having a boron atom shielded byfour, perfluorinated polycyclic radicals. Selected metallocene-NCAcombinations may assist in preserving higher molecular weights and/orhigher operating temperatures. Thus they may be among the preferredcatalyst for the interpolymers of the invention. By operating thecontinuous process in solution at unusually high process temperaturesand/or monomer conversions, surprisingly high levels of LCB may beachieved.

Another advantage to using propylene as a comonomer in wire and cableapplications pertains to its high filler holding capacity that is aresult of the higher plateau modulus of the polymer relatively to higheralpha olefin copolymers. Copolymers with short side chains are lesscoiled and more extended. This higher radius of gyration leads to highernumber of entanglements with neighboring chains and ultimately providesa means of the polymer mixing with and accepting higher levels of fillerand additives. In some applications in wire and cable compounds,especially in low voltage areas, high filler content helps to reduceoverall compound cost.

In yet a further aspect the invention provides an electrical devicecomprising an electrical conductor and a polymeric insulating layercomprising a polymer with any one or more of the features indicatedpreviously or resulting from the process indicated previously.Compositions may be used for the insulting layer including the polymerof the invention in combination with other polymers, fillers etc. as maybe desired for the particular electrical application underconsideration. The insulating member comprising the polymer with thefeatures described previously can be used in various wire an cableapplications. These consist of low voltage, typically less than 5 kV,medium voltage, in the range of 5 kV to 69 kV and high voltage,describing range above 69 kV applications. The compounds in generalcomprise a reinforcing filler, such as calcined clay to providemechanical properties and processability. The amount of filler used inthe formulation depends on the type of application. Sometimes a flameretardant filler, such as magnesium hydroxide, is used in combination orreplacing the calcined clay. The insulating member comprising thepolymer with the features described above can also be used in flameretardant compound applications, wherein an inorganic filler containingwater of hydration is used to provide flame retardant properties.Formulations for medium voltage applications are invariably formulatedwith lead oxide, that seemingly provides good electrical propertiesafter aging. However, reduction or elimination of lead is desirable fromenvironmental considerations. The insulating member comprising thepolymer with features described previously can be used in compounds thatare lead free or contain reduced amounts of lead. For high voltageapplications, the formulations are designed without filler to minimizeelectrical loss. For such compounds, the polymer described previouslycan be used in combination with other polymers to furnish an unfilledcompound that has adequate mechanical properties and processability.Suitably the insulating layer is of a composition also comprising anethylene propylene elastomer with a Mooney [(1+4) 125° C.] range of from10 to 100 and optionally a diene. It is preferred that the elastomer isan ethylene-propylene-vinyl norbornene terpolymer, most preferably witha content of ethylene derived units of from 68-75 wt. %, a molecularweight distribution Mw/Mn of at least 5 and contains from 0.1 to 2.5 wt% of units derived from vinyl norbornene (VNB). Insulating layers may beobtained having a tensile strength of from 5 to 10 MPa min.; a breakelongation of from 150 to 450% and a dielectric constant of less than 4.

EXAMPLES

The invention is illustrated with reference to the Examples. In theExamples the different tests and measurements are performed according tothe protocols below unless otherwise mentioned: TABLE 1 No Test TestMethod Units 1 Ethylene and ASTM D 3900 Wt. % octene content FTIR methodof the polymers See Note * 2 Mooney Viscosity ASTM D 1646-94 Mooneyunits 3 Scorch time ASTM D 2084 - 93 Min. 4 Cure ASTM D 2084-93 DN · mCharacteristics ML DN · m MH Min Ts2 Min T90 DN · m/min Cure Rate DN · mCure State 5 Physical ASTM D 412-92 MPa Properties 100% Modulus MPa 300%Modulus MPa Tensile Strength % Elongation 6 Heat Aging ASTM D 572-88 %Tensile Strength % Elongation 7 Extrusion As described G/minCharacteristics later on in Mass Rate specification μm Ra μm Rt 8Electrical Dissipation Power Loss factor in water @ 90° C., 60 Hz, and600 V AC See Note ** 9 Melt Index and ASTM D 1238 MI g/10 min. MeltIndex MIR Ratio (MIR) Dimensionless 10 Density ASTM D 1505 98 g/cm³ 11ICP AES See Note *** ppm Internally Coupled Plasma Atomic EmissionsSpectroscopy* 1-Octene is measured by reference to the 1387 cm-1 absorbence band ofthe FTIR spectrum.** ASTM D-150-98*** ICP-AES is a commercially available form of optical emissionspectrometry with inductively coupled plasma. The plasma is formed byargon gas flowing through a radio frequency field where it is kept in astate of partial ionization; i.e. the gas contains# electrically charged particles. This allows it to operate at very hightemperatures of up to 10 000 C. At those conditions most elements emitlight of characteristic wavelengths which can be measured and used todetermine the concentration of particular elements.

The sample to be analyzed is introduced into the plasma as a finedroplet aerosol. Light from the different elements is separated intodifferent wavelengths by means of a grating and is captured bylight-sensitive detectors, one for each element being analyzed. Thispermits simultaneous analysis of up to 40 elements. The sensitivity iscomparable to flame atomic absorption with detection limits typically atthe 1 g/L level in aqueous solutions.

Example 1

Polymerization

Copolymerizations were carried out in a single-phase, liquid-filled,stirred tank reactor with continuous flow of feeds to the system andcontinuous withdrawal of products under equilibrium conditions. Allpolymerizations were done in system with a solvent comprisingpredominantly C6 alkanes, referred to generally as “hexane” solvent,using soluble metallocene catalysts and discrete, non-coordinatingborate anion as co-catalysts. An homogeneous dilute solution oftri-n-octyl aluminum in hexane was used as a scavenger in concentrationsappropriate to maintain reaction. No transfer agents, such as hydrogen,were added to control molecular weight. Polymerizations were run at hightemperatures and conversions to maximize macromer re-insertions thatcreate LCB. This combination of a homogeneous, continuous, solutionprocess at higher temperatures helped to ensure that the products hadnarrow composition and sequence distributions, but higher long chainbranching content as measured by MIR(I21/I2).

The hexane solvent was purified over beds of 3A mole sieves and basicalumina. Ethylene and octene were dried over beds of 3A mole sievesonly. All feeds were pumped into the reactors by metering pumps, exceptfor the ethylene, which flowed as a gas through a mass flowmeter/controller. Reactor temperature was controlled adiabatically bycontrolled chilling of the feeds and using the heat of polymerization toheat the reactor. Feed temperature can range from −20° C. to 40° C. orhigher. Typical feed temperatures are kept at 10° C. for high conversionruns and as high as 25° C. for high temperature runs.

The reactors were maintained at a pressure in excess of the vaporpressure of the reactant mixture to keep the reactants in the liquidphase. In this manner the reactors were operated liquid full in ahomogeneous single phase. Ethylene and propylene feeds were combinedinto one stream and then mixed with a pre-chilled hexane stream. Ahexane solution of a tri-n-octyl aluminum scavenger was added to thecombined solvent and monomer stream just before it entered the reactorto further reduce the concentration of any catalyst poisons. A mixtureof the catalyst components in solvent was pumped separately to thereactor and entered through a separate port.

The reaction mixture was stirred aggressively using a magna-drive systemwith three directionally opposed tilt paddle stirrers set to about 750rpm to provide thorough mixing over a broad range of solutionviscosities. Flow rates were set to maintain an average residence timein the reactor of about 10 minutes. On exiting the reactor the copolymermixture was subjected to quenching, a series of concentration steps,heat and vacuum stripping and pelletization.

The general conditions may be as described in WO 99/45041 incorporatedherein for US purposes. Water is then supplied to kill thepolymerization reaction, which might otherwise continue in the presenceof surviving catalyst, unreacted monomer, and elevated temperature.

To obtain the highly branched polymers of the invention, the temperatureis raised to an extra-elevated level by the use of a selected catalystsystem. The catalyst system is selected to provide a good hightemperature stability and to incorporate comonomer and macromer readily.By using the higher temperatures differences in incorporation ofcomonomers and/or macromers due to molecular size are reduced favoringLCB production. In addition monomer and comonomer conversion can beincreased limiting the amount of monomer and comonomer available forpolymerization and again favoring macromer incorporation and LCBformation.

Increased temperatures can be reached in adiabatic operation byincreasing the amount of monomer and comonomer converted to polymer perunit time using increased levels of catalyst and increased monomerconcentrations. Increased polymerization temperatures may themselves beassociated with increased activity so that the catalyst addition ratemay need to be changed to reach stable operating conditions. Increasedmonomer conversions may be reached by increasing catalyst levels orincreasing the reactor residence times without increasing the monomerconcentration so that monomer is consumed to a greater extent and itsconcentration lowered. Optimally the catalyst system is selected topermit both higher monomer conversion and maintained or improvedoperating temperatures.

The effluent of the continuous stirred tank reactor is passed to heatexchangers to raise the temperature to 220° C. Liquid phase separationis then effected by a rapid pressure drop as the polymerization mixturepasses through a let-down valve in a liquid phase separation vessel, inwhich the pressure drops quickly from 100 Bar to 40 Bar. Inside thevessel an upper lean phase is formed with less than 0.1 wt % of polymerand a lower polymer rich phase with 30 to 40 wt % of polymer. Theconcentration in the polymer rich phase is approximately double totriple that in the polymerization effluent. After further removal ofsolvent and monomer in a low-pressure separator and devolatilizer,pelletized polymer can be removed from the plant.

The lean phase and volatiles removed downstream of the liquid phaseseparation are recycled to be part of the polymerization feed. In theprocess a degree of separation and purification takes place to removepolar impurities that might undermine the activity of the catalyst. Anyinternally unsaturated olefins, which are difficult to polymerize wouldgradually build up in the lean phase and recycle streams. Any adverseeffects on the polymerization activity, may be mitigated by removingthese olefins from the recycle stream and/or encouraging theirincorporation in the polymer, favored by high polymerizationtemperatures.

The following runs were performed with the following catalyst systems:TABLE 2 Catalyst Transition metal Activator Component Scavenger systemcomponent (TM) (NCA) component (A) Dimethyl silyl Dimethyl aniliniumTri-n-octyl bis(indenyl) tetrakis (heptafluoro- aluminum hafniumdimethyl naphthyl) borate (B) (p-Et₃Si-phenyl)₂C Dimethyl aniliniumTri-n-octyl (2,7^(t)Bu)₂Flu)(Cp) tetrakis (heptafluoro- aluminum HfMe₂naphthyl) borate (C) (p-Et₃Si-phenyl)₂C Dimethyl anilinium Tri-n-octyl(2,7^(t)Bu)₂Flu)(Cp) tetrakis aluminum HfMe₂ (pentafluorophenyl) borate

Plastomers are made in a number of runs using the process generallydescribed previously and the indicated catalyst systems. TABLE 3 Co- Runmonomer Cat/Act C² wt % Density MI MIR I Propylene (A) 73.4 0.872 0.9652.9 II Propylene (A) 74.6 0.875 1.18 46.3 III Propylene (B) 73.3 0.8711.21 64.2 IV Octene (C) 67.5 0.872 3.8 36.4 Comp. V Octene (C) 72.90.885 1.0 44.2 Comp.

No hydrogen was added. The process conditions in the runs were eithervaried to achieve the target MI by adjusting the temperature OR byadjusting the monomer conversions as shown in the following details. Theprocess conditions are summarized in Table 4. TABLE 4 (Average valuesfrom experimental runs) C² C³ Production g polymer/g Run Process Controlconversion conversion Rx Temp Rate TM I High Conversion 84.7% 43.3%.146° C. 11.6 Kg/hr 250 000 II High Rx Temp 70.0% 27.5%. 156° C. 9.8Kg/hr 422 000 III High Conversion and  90.4%. 56.3%. 160° C. 12.4 Kg/hr203 000 High Temperature IV High Conversion 90.9% 59.9%  145.5° C.  12.1Kg/hr 103 000 Comp V High temperature  84.0%. 48.2%. 153.5° C.  11.7Kg/hr 110 000 Comp. VI Typical run (not   76%  38% 130° C. Not  90 000according to available invention)

Octene used as comonomer may include isomers, which have a negativeeffect on activity. TABLE 5 (Specific values from samples during run)MI(190 Activity ICP ICP Sample Catalyst Monomer Process ° C., 2.16 MIR gpoly./g Boron Hafnium No type feed Control kg) (I₂₁/I₂). TM ppm ppm I(A) C² + C³ High 0.98 54.03 268 800 N/A N/A conversion II (A) C² + C³High 1.25 43.35 425 000 <0.22 0.826 reaction temp HI (B) C² + C³ High1.56 78.66 204 700 N/A conversion VI (C) C² + C⁸ Typical run 1.06 28.76 90 000  0.14* 2.1* Comp. (not acc. to invention)*not measured by ICP, calculated on a 100% inclusion of catalyst residuein polymer.

Table 4 illustrates that using the dimethyl anilinium tetrakis(pentafluorophenyl) borate as NCA, leads to low activities and hencenegative impact on electrical properties (run 4 and 5).(p-Et³Si-phenyl)2C(2,7tBu)2Flu)(Cp)HfMe2 provides a higher conversionand promotes a high MIR(I²¹/I²) value. Using a catalyst system with achiral or achiral hafnocene hence permits the production of a polymer,which has a commercial MI range, a high MIR(I²¹/I²) and a low catalystresidue in the polymer.

Example I shows a high conversion and reasonable activity. TheMIR(I21/I2) was 53. Example II is made at a high polymerizationtemperature at some reduction in conversion. The MIR(I21/I2) at 46remains high and activity is much higher than for I. Example III showsthat the use of catalyst (B) permits a higher conversion/temperaturebalance than catalyst (A) at comparable activity. The choice of processconditions and catalyst permits the combination of a high conversion,high polymerization temperature and high MIR(I21/I2). Example IV and Vshow that using octene-1 as a comonomer does not permit a goodcombination of high activity and high MIR(I21/I2).

Blend with the Interpolymers with EP-VNB

Table 6 contains a list of the ethylene α-olefin polymers used in themedium voltage electrical formulation also containing Vistalon V1703Pcommercially available from ExxonMobil Chemical company. This polymercontains vinyl norbornene (VNB) as the termonomer and is highlybranched. TABLE 6 POLYMER CHARACTERISTICS ML MI (I + 4) C² (g/10 MIR125° C. Diene Diene Polymer type (wt. %) g/ml min) (I₂₁/I₂) (MU) Type(wt. %) Vistalon ® C³ 76 0.870 25 VNB 0.9 1703P III C³ 73.6 0.872 1.3 68None None Engage 8100 C⁸ 62 0.870 1.0 28 23 None None

Metallocene polymers IV and VI are comparative ethylene octene polymersmade with dimethyl anilinium tetrakis (pentafluorophenyl) borate as anactivator at a density of 0.870. III is an inventive ethylene propylenecopolymer prepared using a metallocene catalyst and dimethyl aniliniumtetrakis (heptafluoro-naphthyl) borate as activator. Engage 8100 is anethylene octene copolymer commercially available from DuPont DowElastomers LLC.

Table 7 shows an industry standard medium voltage insulation compoundcontaining 60 parts of clay as filler. TABLE 7 MEDIUM VOLTAGE COMPOUNDFORMULATION Components Description Formulation (phr) Polymer¹ 100Translink 37 Clay Calcined Clay 60 Agerite MA Antioxidant 1.5 Drimix A172 Vinyl Silane 1.0 Zinc Oxide 5.0 ERD 90 Red Lead 5.0 Escorene LD 400Low Density Polyethylene 5.0 Paraffin 1236 Wax 6.0 Curatives DiCup 40 KEDicumyl Peroxide 6.5 (40% Active)¹III + V 1703P

The clay, Translink 37 is calcined, surface treated Kaolin availablefrom Engelhard Corp. The formulations were compounded using a two passmixing protocol in a 1600 ml. Banbury mixer using a batch weight of 1420g, which corresponds to a fill factor of 75%. The masterbatch compoundwithout the peroxide was mixed in the first pass for a total mixing timeof 7 minutes following the mixing procedure shown in Table 8. Themasterbatch discharged from the Banbury mixer was sheeted out on atwo-roll mill. The batch was homogenized several times on the mill. Themill temperature was maintained around 90° C. during mixing. The milledmasterbatch was cut into small strips using a mill knife. The stripswere introduced again into the mixer along with the peroxide, and thecompound was mixed for further two minutes at temperatures less than125° C. The final compound was homogenized once again on the two-rollmill and granulated into small pieces for extrusion processing.

Table 8 shows the mixing procedures and conditions. TABLE 8 MIXINGPROCEDURE Equipment: 1600 cc. Banbury Batch Size: 1420 gm Time Rotor(minutes) Speed (rpm) Ingredients Addition 0 85 Polymer + Agerite 0.5 85½ Clay, Zinc Oxide ERD 90, ½ Drimix LD 400 2.0 100 ¼ Clay, ¼ Drimix, ½Wax 3.0 100 ¼ Clay, ¼ Drimix, ½ Wax 4.0 100 Sweep 5.5 100 Sweep 7.0 Dump

Compound extrusion studies were performed in a HAAKE Rheocord 90 singlescrew extruder. The screw length to diameter (LID) for this extruder is20/1. The extruder screw has a compression ratio of 2/1, which istypical for processing rubber compounds. A cylindrical die with a landlength of 9.5 mm and diameter of 3.2 mm was used to assess surfaceappearance of the extrudates. The various zones of the extruder and thedie block temperature are maintained constant at 125° C. Granulatedrubber is fed through the extruder hopper to maintain a full screw, butan empty hopper during extrusion. The extruder screw speed is variedfrom 25 RPM to 100 rpm. The mass throughput is measured at every screwspeed by collecting a sample of the extrudate over a specific length oftime, typically 10 to 30 seconds depending on the screw speed. At leastthree samples are collected to provide an average value.

The surface roughness of the extrudate is analyzed using a Surfcom 110surface gauge. The Surfcom instrument is equipped with a diamond stylusthat traverses over the surface of the extrudate under examination,recording the surface irregularities. The vertical distance between thehighest and lowest point in a surface irregularity, denoted as Rt (□m)is measured for every sample. The arithmetic mean Ra, denoting thedeparture of the surface profile from a mean line is also recorded (□m).An average value is obtained based on at least 3 measurements persample.

The variation of compound viscosity with frequency was measured using aRPA 2000 Rubber Process Analyzer. The measurements were made at aconstant strain of 14% and temperature of 125° C. The frequency wasvaried from 0.21 to 219 (1/sec).

Table 9 shows the compound cure and physical properties of mediumvoltage compound formulations, prepared as outlined in Tables 7 and 8,containing the EP(D)M-VNB terpolymer V 1703P by itself and in blendswith the metallocene ethylene propylene copolymer III. TABLE 9 COMPOUNDCURE CHARACTERISTICS AND PHYSICAL PROPERTIES FORMULATION EXAMPLE 1 Comp2 3 4 V 1703P 100 50 25 III 0 50 75 100 CMPD. MOONEY MU 22 22 2{graveover ( )}1 18 VISCOSITY (ML) (1 + 4) 125 C. Mooney Scorch (Ms) 132 C.Min Value MU 10.8 10.6 9.8 8.4 Time for 3 point min 14.2 18.5 20.5 21.7rise ODR 200 C. (392 F.), 3 deg, 6 min ML dN-m 6.1 6.3 5.9 5.1 MH dN-m94.1 83.6 76.3 69.0 Ts2 min 0.63 0.62 0.65 0.65 T90 min 1.84 1.86 1.942.0 T98 min 2.38 2.36 2.43 2.47 Rate dN-m/min 110.4 86.5 72.8 61.5 MH-MLdN-m 88.0 77.3 70.5 63.9 Press Cure, 20 min @ 165 C. (329 F.) HardnessShore A 89 86 86 85 100% Modulus MPa 5.3 5.0 4.4 3.9 200% Modulus MPa8.7 8.1 7.3 6.4 300% Modulus MPa 10.7 8.4 Tensile Strength MPa 10.3 9.29.0 8.6 Elongation % 287 263 267 303 Heat Aging (14 d/ 150 C.) Hardness(oven #4) Shore A 88 86 86 84 Hardness Change Points −1 0 0 −1 TensileStrength MPa 1451 1297 1278 1142 Tensile Retain % 97 97 98 92 Elongation% 267 282 299 359 Elongation Retain % 93 107 112 118

Formulation example 1 is a comparative formulation, while Formulationexamples 2 through 4 are inventive compounds. Substitution of V 1703Pwith the metallocene candidate III leads to a marginal decrease in curerate from the replacement of the VNB terpolymer, but enhanced heat agedphysical properties, notably elongation to break.

Table 10 shows compound extrusion properties of the formulationdescribed in Table 9. TABLE 10 Example 1 Comp 2 3 4 V 1703P 100 50 25III 0 50 75 100 HAAKE Rheocord 125 g/min C., Mass Rate 25 RPM 36 39 3434 50 RPM 65 51 69 51 75 RPM 110 100 107 103 100 RPM 122 93 108 106HAAKE Rheocord 125 □m C., R_(a) 25 RPM 16 4 13 26 50 RPM 7 2 17 18 75RPM 8 2 15 29 100 RPM 7 2 27 24 HAAKE Rheocord 125 □m C., R₁ 25 RPM 7526 76 154 50 RPM 44 16 111 113 75 RPM 50 17 83 154 100 RPM 42 18 181 147

At the 50/50 blend ratio of V 1703P to III in the compound (Formulationexample 2), the extrudate surface properties are comparable to thecomparative Example 1 formulated with the reference polymer V 1703P.With increasing metallocene polymer content in the formulation, meltfracture was noticed on the extrudates at extruder speed of 50 rpm andabove. This is manifested by the relatively high Rt values for Examples3 and 4.

FIG. 1 shows the variation of the compound dissipation (or loss) factorwith time on samples that were aged in water at 90° C. The performanceof the inventive formulations 2 through 4 is very similar to thecomparative formulation example 1.

FIG. 2 shows the variation of compound viscosity with frequency informulations featuring the reference polymer V 1703P by itself, and in50/50 blends with the metallocene candidate III and comparativemetallocene polymers PX-3 and ENGAGE 8100. The extensive branching inthe reference polymer V 1703P makes the compound containing this polymermost shear sensitive resulting in the lowest compound viscosity at thehigher frequency range of 100 to 250 sec-1. The compounds featuring thecomparative polymers VI and ENGAGE 8100 are the least shear sensitive.These formulations would be somewhat defensive in processabilitydisplaying melt fracture characteristics at low shear stress. Theformulation featuring the metallocene polymer III shows enhancedprocessability over the comparative VI and ENGAGE 8100 containingcompounds. These interpolymers may be pelletized directly.

Formulation Examples 5 to 7

Medium voltage electrical compounds featuring polymer blends of themetallocene candidate III with V 1703P were formulated as per theformulation in Table 7, at varying blend ratios of III to V 1703 P. Theformulations were granulated into fine pellets and extruded onto a 14AWG copper wire.

Table 11 shows the process conditions for the wire line extrusion, whichcorrespond to typical run conditions of the control compound featuringthe V 1703P polymer. The medium voltage insulation compound coating thewire was vulcanized in the steam/water heated continues vulcanizationtube maintained at a constant temperature of 208° C. Typical residencetime in the vulcanization tube depends on the line speed. At a linespeed of 12.2 m/min, the residence time is 1.65 minutes.

As seen in Table 11 all the inventive formulations varying in blendratio of III to V 1703 P processed well at conditions similar to thecontrol compound. TABLE 11 WIRE LINE PROCESS CONDITIONS M313101corresponds to run III. EXAMPLE 5 6 7 M3013101/V 1703 P Ratio 100/075/25 50/50 Body (Actual/Set) C 105/104 104/104 105/105 Die C 103/102105/105 112/102 Zone 1 C 99/99 98/98 98/98 Zone 2 C 100/100 100/100100/100 Zone 3 C 102/102 102/102 102/102 Clamp C 102/102 102/102 103/103Flange C 103/102 105/105 102/102 Melt Temperature C 116 117 115 LineSpeed m/min 12.2 12.2 12.2 Line Speed Master % 88 88 88 Extruder Ref %75 75 70 Capstan Ref % 55 55 55 Extruder RPM RPM 66 66 61.7 ExtruderHead Pressure MPa 14.5-18.6 17.2-22.1 14.5-19.3 Steam Pressure MPa 1.721.72 1.72 CV Cure Temp C. 208 208 208 Water Level m 6.4 6.4 6.4

Table 12 shows the physical properties of the wire samples of Table 11containing varying blend ratios of the metallocene candidate M3013101 toV 1703P. Formulation example 8 is the control formulation featuring V1703P without the metallocene candidate. As seen in Table 12, thesurface roughness of the wire samples (Rt) is nearly the same in all thecompounds. The melt fracture seen in Formulation examples 5 and 6 onextruded compounds (Table 10) is eliminated by the application of steamin the continuous vulcanization tube. All the example formulations 5though 7 achieve close to 90% cure, comparable to the control Example 8.The tensile strength of the inventive compounds is slightly lower thanthe control, but this level is adequate for the end use application.TABLE 12 PROPERTIES OF EXTRUDED WIRE EXAMPLE 5 6 7 8 M3013101/V 1703P100/0 75/25 50/50 0/100 Line Speed m/min 12.2 12.2 12.2 13.4 CureTemperature ° C. 208 208 208 208 Wire Surface Roughness □m Ra 1.75 1.391.88 1.43 Rt 19.22 16.27 20.57 12.38 Ra + 0.1 Rt 3.67 3.02 3.94 2.67Cross Linked Material % 90 92 88 90 100% Modulus MPa 2.1 2.3 2.6 3.3200% Modulus MPa 2.7 3.0 3.4 4.1 Tensile Strength MPa 9.0 8.6 9.4 11.0Elongation % 390 299 292 291 Break Down Strength KV/mm 33 33 31 56

In certain embodiments, the processes. Polymers, and formulationsdescribed herein enable the production of compositions and electricaldevices capable of exhibiting beneficial electrical properties in theabsence of a lead oxide compound or at reduced levels of a lead oxidecompound. Specifically, in certain embodiments, the beneficialelectrical properties are dissipation factors and dielectric constants.A series of experimental evaluations were conducted to evaluate theseelectrical properties for formulations incorporating certain polymericmaterials described herein.

Table 13 lists three medium voltage compound formulations, prepared asoutlined in Tables 7 and 8, for which the electrical properties wereevaluated. Each formulation includes an ethylene interpolymer identifiedas Polymer IV or Polymer V.

Polymer IV is an EPDM terpolymer produced in a Ziegler-Natta catalyzedpolymerization. Polymer IV has a Mooney viscosity of ML (1+4) at 125° C.of 25. The terpolymer incorporates ethylene, propylene, and ethylideneat weight percentages of 73.3 wt. %, 23.4 wt. %, and 3.3 wt. %,respectively. Polymer IV is commercially available from ExxonMobilChemical under the designation Vistalon® 8731.

Polymer V is an EPM copolymer (ethylene-propylene copolymer) producedusing a continuous polymerization process incorporating a metallocenecatalyst and dimethyl anilinium tetrakis (heptafluoro-naphthyl) borateas activator. Polymer V has a Mooney viscosity of ML (1+4) at 125° C. of16 and a melt index of 1 (g/10 min.). Polymer V incorporates ethyleneand propylene at weight percentages of 72 wt. % and 28 wt. %respectively. TABLE 13 Example 9 Example 10 Example 11 Components (phr)(phr) (phr) Polymer IV 100 100 0 Polymer V 0 0 100 Translink 37 clay 6060 60 Zinc oxide 5 5 5 ERD 90 0 5 0 Paraffin wax 5 5 5 Escorene LD 400 55 5 Agerite Resin D 1.5 1.5 1.5 Drimix A 172 1 1 1 Silane DiCup 40KE 6.56.5 6.5 Total phr 184 189 184Curing conditions for all formulations was 20 minutes at 165° C

Dissipation factors for Examples 9-11 were determined over time asreported in Table 14. Dissipation factors were determined after aging inwater at 90° C. in accordance with ASTM D-150-98. TABLE 14 Time Example9 Example 10 Example 11 0 0.0054 0.0055 0.0054 1 day 0.0169 0.01650.0118 8 days 0.0249 0.0153 0.0106 14 days 0.0243 0.0160 0.0111 21 days0.0233 0.0146 0.0116 28 0.0242 0.0127 0.0113600 volts, ASTM tensile pad

Generally, the lower the dissipation factor, the better the electricalproperty of the formulation. For ease of analysis, the dissipationfactors over time for the formulations of Examples 9-11 are plotted inFIG. 3. As seen by reference to Table 14 and FIG. 3, the formulationincorporating Polymer IV demonstrated improved dissipation factorproperties resulting from the inclusion of 5 phr of a lead oxidecompound (ERD 90). However, the formulation of Example 11, incorporatingmetallocene catalyzed Polymer V, demonstrated superior dissipationfactor performance even without the addition of or presence of lead, ora derivative thereof, such as a lead oxide compound.

In certain embodiments, the formulations described herein aresubstantially free of lead, and derivatives thereof. For purposes ofthis disclosure, the term substantially free of lead and derivativesthereof shall mean formulations having less than 0.1 phr lead and/orderivatives thereof, including, but not limited to lead oxides, per 100phr polymeric material(s) in the composition. In certain embodiments,the formulations described herein are substantially free of lead, andderivatives thereof and have dissipation factors of less than 0.02 afteraging for 28 days in water at 90° C. In other embodiments, theformulations described herein are substantially free of lead, andderivatives thereof, and have dissipation factors of less than 0.15after aging for 28 days in water at 90° C. In still other embodiments,the formulations described herein are substantially free of lead, andderivatives thereof, and have dissipation factors of less than 0.13after aging for 28 days in water at 90° C.

Dielectric constant values of the formulations of Examples 9-11 weredetermined over time as reported in Table 15. Dielectric constant valueswere determined after aging in water at 90° C. in accordance with ASTMD-150-98. TABLE 15 Time Example 9 Example 10 Example 11 0 2.58 2.58 2.571 day 2.45 2.50 2.37 8 days 2.53 2.53 2.39 14 days 2.54 2.54 2.39 21days 2.58 2.56 2.40 28 2.59 2.56 2.42600 volts, ASTM tensile pad

Generally, the lower the dielectric constant, the better the electricalproperty of the formulation. The formulations of Examples 9 and 10,incorporating Polymer IV, with and without incorporation a lead oxide,exhibited relatively stable dielectric constants over the 28-day period.The formulation of Example 11, incorporating the metallocene catalyzedcopolymer, Polymer V, and no added lead oxide, demonstrated a superiorlower dielectric constant after one day and a favorable dielectricconstant reduction of more than 5% by the end of the 28 day period.

In certain embodiments, the formulations described herein aresubstantially free of lead, and derivatives thereof, and have dielectricconstant values of less than 2.55 after aging for 28 days in water at90° C. In other embodiments, the formulations described herein aresubstantially free of lead, and derivatives thereof, and have dielectricconstant values of less than 2.50 after aging for 28 days in water at90° C. In still other embodiments, the formulations described herein aresubstantially free of lead, and derivatives thereof, and have dielectricconstant values of less than 2.45 after aging for 28 days in water at90° C.

Tradenames used herein are indicated by a ™ symbol, or an ® symbol,indicating that the names may be protected by certain trademark rights.Some such names may also be registered trademarks in variousjurisdictions.

All patents, test procedures, and other documents cited herein,including priority documents, are fully incorporated by reference to theextent such disclosure is not inconsistent with this invention and forall jurisdictions in which such incorporation is permitted.

While the illustrative embodiments of the invention have been describedwith particularity, it will be understood that various othermodifications will be apparent to and can be readily made by thoseskilled in the art without departing from the spirit and scope of theinvention. Accordingly, it is not intended that the scope of the claimsappended hereto be limited to the examples and descriptions set forthherein but rather that the claims be construed as encompassing all thefeatures of patentable novelty which reside in the present invention,including all features which would be treated as equivalents thereof bythose skilled in the art to which the invention pertains.

When numerical lower limits and numerical upper limits are listedherein, ranges from any lower limit to any upper limit are contemplated.

1. A continuous polymerization process for preparing a random ethyleneinterpolymer, the process comprising: (A) polymerizing ethylene, and anα-olefin comonomer selected from the group consisting of propylene and1-butene and mixtures thereof under continuous random polymerizationconditions in the presence of single site catalyst system employing anionic activator having cyclic ligands shielding a central charge bearingatom, at a temperature of from 140° C. to 250° C. at a conversion ofethylene of from 80 to 99% and a comonomer conversion of at least 20%and (B) devolatilizing the polymer to provide an ethylene copolymerhaving a density of from 0.85 to 0.92 g/cm³, an MI of from 0.01 to 100g/10 min and an MIR(I²¹/I²) of from 30 to
 400. 2. The process of claim1, wherein the comonomer conversion is from 30 to 80%.
 3. The process ofclaim 1, wherein the ethylene copolymer has an MI of 0.1 to 20 g/10 minand an MIR(I²¹/I²) of from 30 to
 200. 4. The process of claim 1, whereinthe ratio of MIR(I²¹/I²) over MI is from 2 to
 9000. 5. The process ofclaim 1, wherein “a” in the following expressionMIR(I₂₁/I₂)=[a*(MI){circumflex over ( )}−0.167] is from 42 to
 440. 6.The process of claim 1, wherein the interpolymer contains at least 55mol % of ethylene derived units.
 7. The process of claim 1, wherein theinterpolymer contains at least 60 mol % of ethylene derived units. 8.The process of claim 1, wherein the interpolymer contains from 0 to lessthan 10 mol % of a α-olefin comonomer other than propylene and 1-butenefrom 0 to less than 0.5 mol % of a diene.
 9. The process of claim 1,wherein the interpolymer contains from 0 to less than 5 mol % of aα-olefin comonomer other than propylene and 1-butene and from 0 to lessthan 0.1 mol % of a diene.
 10. The process of claim 1, wherein thepolymerization is performed adiabatically using a catalyst systemincluding a hafnocene having two ligands with cyclopentadienyl-typegroups connected by a bridging structure having a single atom bonded toeach of the cyclopentadienyl type ligands.
 11. The process of claim 1,wherein the ionic activator has at least two ligands that are polycyclicand at least partly fluorinated.
 12. The process according to claim 1wherein the ionic activator has four fluorinated polycyclic ligands. 13.The process according to claim 1 wherein the ionic activator is dimethylanilinium tetrakis (heptafluoro-naphthyl) borate.
 14. The process ofclaim 1, wherein the polymerization is performed in the substantialabsence of transfer agent such as hydrogen.
 15. The process of claim 1,wherein the heat of polymerization raises the temperature by at least100° C. between the feed for the continuous polymerization and theeffluent for devolatilization.
 16. The process of claim 1, wherein thepolymerization is performed in a series reactor to provide a multimodalmolecular weight distribution or composition distribution.
 17. Acontinuous polymerization process for preparing a random ethyleneinterpolymer, the process comprising: (A) polymerizing ethylene, and anα-olefin comonomer selected from the group consisting of propylene and1-butene and mixtures thereof under continuous random polymerizationconditions in the presence of hafnocene complex having twocyclopentadienyl groups connected by a single atom bridging structureand an ionic activator having cyclic ligands shielding a central chargebearing atom with at least two of such ligands being polycyclic and atleast partly fluorinated, at a temperature of 140° C. to 250° C.adiabatically in a continuous polymerization reactor in the substantialabsence of transfer agent such as hydrogen at a conversion of ethyleneof 80 to 99% and a comonomer conversion of from 20 to 80%; and (B)devolatilizing the polymer to provide an ethylene copolymer having adensity of from 0.85 to 0.92 g/cm³, an MI of from 0.01 to 100 g/10 minand an MIR(I²¹/I²) of from 30 to
 400. 18. The process of claim 17,wherein the polymerization is performed in a series reactor arrangementto provide a multimodal molecular weight distribution or compositiondistribution.
 19. An ethylene interpolymer comprising units derived froman α-olefin comonomer selected from the group consisting of propyleneand 1-butene and mixtures thereof, having a density of from 0.85 to 0.92g/cm³, an MI of from 0.01 to 100 g/10 min and an MIR(I²¹/I²) of from 30to 400, which is obtained by solution polymerization using transitionmetal complex as a catalyst and a non-coordinating anion, and has alevel of NCA derived residue as determined by boron content less than0.5 ppm (parts per million parts of polymer) as determined by ICP. 20.The interpolymer of claim 19, wherein the interpolymer has a level ofNCA derived residue as determined by boron content undetectable by ICP.21. The interpolymer of claim 19, wherein the interpolymer contains atleast 55 mol % of ethylene derived units.
 22. The interpolymer of claim19, wherein the interpolymer contains at least 60 mol % of ethylenederived units.
 23. The interpolymer of claim 19, wherein theinterpolymer has an MI of from 0.01 to 0.55 and anMIR(I²¹/I²)>−90.9×MI+90.
 24. The interpolymer of claim 19, wherein theinterpolymer has an MI of from 0.55 to 8 and anMIR(I²¹/I²)>−1.3×MI+40.7.
 25. The interpolymer of claim 19, wherein theinterpolymer has an MI of from 8 to 100 and an MIR(I²¹/I²)>30.
 26. Theinterpolymer of claim 19, wherein the interpolymer has an MI of from 0.5to 15 and an MIR(I²¹/I²) of from 30 to
 100. 27. The interpolymer ofclaim 19, wherein the interpolymer has an MI of from 0.5 to 15 and anMIR(I²¹/I²) of from 40 to
 100. 28. The interpolymer of claim 19, whereinthe interpolymer has an MI of from 0.01 to 2 and an MIR(I²¹/I²) of from40 to
 150. 29. The interpolymer of claim 19, wherein the interpolymerhas an MI of from 0.01 to 2 and an MIR(I²¹/I²) of from 50 to
 100. 30.The interpolymer of claim 19, wherein the ratio of MIR(I²¹/I²) over MIis from 2 to
 9000. 31. The interpolymer of claim 19, wherein “a” in thefollowing expression MIR(I²¹/I²)=[a*(MI){circumflex over ( )}−0.167] isfrom 42 to
 440. 32. The interpolymer of claim 19, wherein theinterpolymer has an MI of from 0.01 to 0.30 and anMIR(I²¹/I²)>−103.45×MI+91.0.
 33. The interpolymer of claim 19, whereinthe interpolymer has an MI of from 0.01 to 0.30 and anMIR(I²¹/I²)<−103.45×MI+241.0.
 34. The interpolymer of claim 19, whereinthe interpolymer has an MI of from 0.30 to 1.40 and anMIR(I²¹/I²)>−18.18×MI+65.4.
 35. The interpolymer of claim 19, whereinthe interpolymer has an MI of from 0.30 to 1.40 and anMIR(I²¹/I²)<−18.18×MI+215.4.
 36. The interpolymer of claim 19, whereinthe interpolymer has an MI of from 1.40 to 8.0 and anMIR(I²¹/I²)>−1.515×MI+42.1.
 37. The interpolymer of claim 19, whereinthe interpolymer has an MI of from 1.40 to 8.0 and anMIR(I₂₁/I₂)<−1.515×MI+192.1.
 38. The interpolymer of claim 19, whereinthe interpolymer has an MI of from 8.0 to
 100. 39. The interpolymer ofclaim 19, wherein the interpolymer has an MI of from 8.0 to 100 and anMIR(I²¹/I²) of from 30 to
 180. 40. The interpolymer of claim 19, whereinthe single site catalyst is a transition metal complex of a Group IVmetal selected from the group consisting of Zr and Hf.
 41. Theinterpolymer of claim 19, wherein the single-site catalyst is a Hafniumcontaining complex.
 42. The interpolymer of claim 19, wherein the levelof single site catalyst residue as measured by the content of transitionmetal is less than 2 ppm (parts per million parts of polymer).
 43. Theinterpolymer of claim 19, wherein the level of single site catalystresidue as measured by the content of transition metal is less than 1ppm (parts per million parts of polymer) as determined by ICP.
 44. Theinterpolymer of claim 19, wherein the density is at least 0.86 and lessthan 0.89 g/cm³.
 45. The interpolymer of claim 19, wherein the densityis at least 0.87 and less than 0.88 g/cm³.
 46. The interpolymer of claim19, wherein the interpolymer contains from 0 to less than 10 mol % of aα-olefin comonomer other than propylene and 1-butene and wherein theinterpolymer contains from 0 to less than 0.5 mol % of a diene.
 47. Theinterpolymer of claim 19, wherein the interpolymer contains from 0 toless than 5 mol % of a α-olefin comonomer other than propylene and1-butene and wherein the interpolymer contains from 0 to less than 0.1mol % of a diene.
 48. The interpolymer of claim 19, wherein theinterpolymer contains from 0 to less than 0.1 wt % of ananti-agglomeration additive, such as a stearate salt.
 49. Theinterpolymer according to claim 19 wherein the NCA derived residue isderived from an ionic activator having at least two polycyclic ligands,preferably at least partly fluorinated.
 50. The interpolymer accordingto claim 19 wherein the NCA derived residue is derived from an ionicactivator having four fluorinated polycyclic ligands.
 51. Theinterpolymer according to claim 19 wherein the NCA derived residue isderived from a dimethyl anilinium tetrakis (heptafluoro-naphthyl) borateionic activator.
 52. An ethylene interpolymer comprising: at least 55mol % of ethylene derived units; and a balance of units derived from anα-olefin comonomer selected from the group consisting of propylene and1-butene and mixtures thereof and from 0 to less than 5 mol % of aα-olefin comonomer other than propylene and 1-butene and from 0 to lessthan 0.1 mol % of a diene, having a density of from 0.85 to 0.92 g/cm3,an MI of from 0.01 to 100 g/10 min and an MIR(I₂₁/I₂) of from 30 to 400,which is obtained by solution polymerization using transition metalcomplex as a catalyst and a non-coordinating anion, and has a level ofNCA derived residue as determined by boron content less than 0.5 ppm(parts per million parts of polymer) as determined by ICP and the levelof single site catalyst residue as measured by the content of catalystderived transition metal is less than 2 ppm as determined by ICP.
 53. Anelectrical device comprising an electrical conductor and a polymericinsulating layer comprising an ethylene interpolymer containing unitsderived from an α-olefin comonomer selected from the group consisting ofpropylene and 1-butene and mixtures thereof, having a density of from0.85 to 0.92 g/cm³, an MI of from 0.01 to 100 g/10 min and anMIR(I₂₁/I₂) of from 30 to 400, which is obtained by solutionpolymerization using transition metal complex as a catalyst and anon-coordinating anion, and has a level of NCA derived residue asdetermined by boron content less than 0.25 ppm (parts per million partsof polymer) as determined by ICP.
 54. The electrical device of claim 53,wherein the insulating layer also comprises an ethylene propyleneelastomer with a Mooney [(1+4) 125° C.] range of from 20 to 50 andoptionally a diene.
 55. The electrical device of claim 53, wherein theelastomer is an ethylene-propylene-vinyl norbornene terpolymer.
 56. Theelectrical device of claim 55, wherein the terpolymer elastomer has acontent of ethylene derived units of from 68-75 wt %, a molecular weightdistribution Mw/Mn as determined by GPC of at least 5 and contains from0.1 to 2.5 wt % of units derived from VNB.
 57. The electrical device ofclaim 53, wherein the insulating layer has a tensile strength of from 5to 10 MPa min., a break elongation of from 100 to 500% and a dielectricconstant of less than
 5. 58. The electrical device of claim 53, whereinthe insulating layer has a tensile strength of from 5 to 10 MPa min., abreak elongation of from 150 to 400% and a dielectric constant of lessthan
 3. 59. An electrical device comprising an electrical conductor anda polymeric insulating layer comprising an ethylene interpolymercomprising at least 55 mol % of ethylene derived units; and a balance ofunits derived from an α-olefin comonomer selected from the groupconsisting of propylene and 1-butene and mixtures thereof, and from 0 toless than 5 mol % of a α-olefin comonomer other than propylene and1-butene and from 0 to less than 0.1 mol % of a diene, having a densityof from 0.85 to 0.92 g/cm³, an MI of from 0.01 to 100 g/10 min and anMIR(I²¹/I²) of from 30 to 400, which is obtained by solutionpolymerization using transition metal complex as a catalyst and anon-coordinating anion, and has a level of NCA derived residue asdetermined by boron content less than 0.25 ppm and as determined by ICP(parts per million parts of polymer) and the level of single sitecatalyst residue as measured by the content of transition metal of lessthan 2 ppm as determined by ICP.
 60. The electrical device of claim 59,wherein the insulating layer also comprises an ethylene propyleneterpolymer elastomer with a Mooney [(1+4) 125° C.] range of from 20 to50 and having a content of ethylene derived units of from 68-75 wt %, amolecular weight distribution Mw/Mn of at least 5 and from 0.1 to 2.5 wt% of units derived from VNB.
 61. A polymeric composition comprising: (i)100 phr of an ethylene interpolymer containing as α-olefin comonomerpropylene and/or 1-butene, having a density of from 0.85 to 0.92 g/cm3,an MI of from 0.01 to 100 g/10 min and an I21/I2 of from 30 to 400obtained by solution polymerization using a transition metal complex asa catalyst and a non-coordinating anion to provide a level of NCAderived residue, as determined by boron content, less than 0.5 ppm asdetermined by ICP, preferably undetectable by ICP; and (ii) less than 5phr of a lead oxide compound.
 62. The polymeric composition of claim 61that is substantially free of lead and derivatives thereof.
 63. Thepolymeric composition according to claim 61 wherein the MI of theinterpolymer is from 0.01 to 0.55 and the I21/I2>−90.9×MI+90.
 64. Thepolymeric composition according to claim 61 wherein the MI is from 0.55to 8 and the I21/I2>−1.3×MI+40.7.
 65. The polymeric compositionaccording to claim 61 wherein the MI is greater than 8 and theI21/I2>30.
 66. The polymeric composition according to claim 61 whereinthe interpolymer contains at least 55 mol % of ethylene derived units.67. The polymeric composition according to claim 61 wherein theinterpolymer contains at least 70 mol % ethylene derived units.
 68. Thepolymeric composition according to claim 61 wherein the interpolymer hasan MI of from 0.5 to 15 and an I21/I2 of from 30 to
 100. 69. Thepolymeric composition according to claim 68 wherein the interpolymer hasa I21/I2 of at least
 40. 70. The polymeric composition according toclaim 61 wherein the ratio of I²¹/I² over MI is from 2 to
 9000. 71. Thepolymeric composition according to claim 61 wherein “a” in theexpression MIR=[a*(MI){circumflex over ( )}−0.167] is from 42 to 440.72. The polymeric composition according to claim 61 wherein theinterpolymer has an MI of from 0.01 to 2 and an I21/I2 of from 40 to150.
 73. The polymeric composition according to claim 72 wherein theinterpolymer has an I21/I2 of at least 50 and/or less than
 100. 74. Thepolymeric composition according to claim 61 wherein the interpolymer hasan MI of from 0.01 to 0.30 and an I21/I2>−103.45×MI+91.0.
 75. Thepolymeric composition according to claim 61 wherein the interpolymer hasan MI of from 0.01 to 0.30 and an I21/I2<−103.45×MI+241.0.
 76. Thepolymeric composition according to claim 61 wherein the interpolymer hasan MI of from 0.30 to 1.40 and an I21/I2>−18.18×MI+65.4.
 77. Thepolymeric composition according to claim 61 wherein the interpolymer hasan MI of from 0.30 to 1.40 and an I21/I2<−18.18×MI+215.4.
 78. Thepolymeric composition according to claim 61 wherein the interpolymer hasan MI of from 1.40 to 8.0 and an I21/I2>−1.515×MI+42.1.
 79. Thepolymeric composition according to claim 61 wherein the interpolymer hasan MI of from 1.40 to 8.0 and an I21/I2<−1.515×MI+192.1.
 80. Thepolymeric composition according to claim 61 wherein the interpolymer hasan MI of from 8.0 to 1000 and an I21/I2>30.0.
 81. The polymericcomposition according to claim 61, wherein the interpolymer has an MI offrom 8.0 to 1000 and an I21/I2<180.0.
 82. The polymeric compositionaccording to claim 61 wherein the single site catalyst is a transitionmetal complex of a Group IV metal, preferably Zr or Hf.
 83. Thepolymeric composition according to claim 61 wherein the level of singlesite residue as measured by the content of transition metal is less than2 ppm as determined by ICP.
 84. The polymeric composition according toclaim 61 wherein the level of single site residue as measured by thecontent of transition metal is less than 1 ppm as determined by ICP. 85.The polymeric composition according to claim 61 wherein the density ofthe interpolymer is at least 0.86 and/or less than 0.89.
 86. Thepolymeric composition according to claim 83 wherein the density of theinterpolymer is at least 0.87 and/or less than 0.88.
 87. The polymericcomposition according to claim 61 wherein the interpolymer contains from0.01 to less than 10 mol % of a α-olefin comonomer other than propyleneand/or 1-butene.
 88. The polymeric composition according to claim 85wherein the interpolymer contains from 0.01 to less than 5 mol % of aα-olefin comonomer other than propylene and/or 1-butene.
 89. Thepolymeric composition according to claim 61 wherein the interpolymercontains from 0 to less than 0.5 mol % of a diene.
 90. The polymericcomposition according to claim 87 wherein the interpolymer contains from0 to less than 0.1 mol % of a diene.
 91. The polymeric compositionaccording to claim 61 wherein the polymer contains less than 0.1 wt % ofan anti-agglomeration additive.
 92. The polymeric composition accordingto claim 61 wherein the NCA derived residue is derived from an ionicactivator having at least two polycyclic ligands, preferably at leastpartly fluorinated.
 93. The polymeric composition according to claim 61wherein the NCA derived residue is derived from an ionic activatorhaving four fluorinated polycyclic ligands.
 94. The polymericcomposition according to claim 61 wherein the polymeric composition hasa dissipation factor of less than 0.02 after aging for 28 days.
 95. Thepolymeric composition according to claim 61 wherein the polymericcomposition has a dielectric constant value of less than 2.50 afteraging for 28 days.
 96. An electrical device comprising an electricalconductor and a polymeric insulating layer comprising a polymer or apolymeric composition according to claim
 61. 97. An electrical deviceaccording to claim 94 wherein the insulating layer also comprises anethylene propylene elastomer with a Mooney (1+4) 125° C. range of from20 to 50 and optionally a diene.
 98. An electrical device according toclaim 95 wherein the elastomer is an ethylene-propylene-vinyl norborneneterpolymer.
 99. An electrical device according to claim 96 wherein theterpolymer has a content of ethylene derived units of from 68-75 wt. %,a molecular weight distribution Mw/Mn of at least 5 and contains from0.1 to 2.5 wt % of units derived from VNB.
 100. An electrical deviceaccording to claim 94 wherein the insulating layer has a tensilestrength of from 5 to 10 MPa min., a break elongation of from 100 to500%, preferably from 150 to 400% and a dielectric constant of less than5.